Method of preparing a thin ceramic composition with two materials, the composition thus obtained and the constituent electrochemical cell and membrane

ABSTRACT

There is disclosed a method for preparing a thin ceramic and/or metallic solid-state composition consisting of three phases: a material (A), a material (B) and pores. The concentration of each phase varies continuously from one face of the article to the other in a continuous and controlled gradient. The porous matrix of material (A) has a porosity gradient of 0% to about 80%, the pores being completely or partly filled with material (B). The concentration of material (B) in the article therefore varies from 80% to 0% of small thicknesses.

BACKGROUND OF THE INVENTION

1. Field of the Invention

The subject of the invention is a novel method for preparing a thinceramic and/or metallic solid-state composition consisting of threephases: a material (A), a material (B) and pores. The concentration ofeach phase varies continuously from one face of the article to the otherin a continuous and controlled gradient. The porous matrix of material(A) has a porosity gradient of 0% to about 80%, the pores beingcompletely or partly filled with material (B). The concentration ofmaterial (B) in the article therefore varies from 80% to 0% of smallthicknesses.

2. Related Art

Porous ceramics have physico-chemical properties, whether thermalstability, chemical stability, biocompatability or mechanical strength,which make them good candidates for various applications such as filtermembranes, sensors, ceramic-to-metal seals, biomaterials, energyconservation, thermal insulation or catalysis. These materials are usedin particular for their low density, their high exchange area and theirhigh permeability thanks to their open porosity.

As techniques for creating porosity in a ceramic, there are:

-   -   incomplete sintering of ceramic particles;    -   the introduction of porosity by emulsion of the material before        sintering;    -   the use of pore formers removed before sintering;    -   forming operations such as extrusion, injection molding, rapid        prototyping; and    -   the use of ceramic fibers.

These methods are listed in Roy W. Rice, “Porosity of ceramics”, MarcelDekker, 1998, pp 20-21.

Incomplete sintering or subsintering of a ceramic powder or of a blendof ceramic powders having different particle sizes does not allow aporosity of greater than 50% to be achieved.

The use of pore formers, removed for example by pyrolysis beforesintering, and leaving pores as the negative thereof in the ceramic, isone of the most appropriate methods for producing materials whoseporosity is controlled in terms of volume fraction, shape and sizedistribution of the pores. Incorporating particulate pore formers, suchas starch, lattices, graphite or resins into ceramic suspensions orslurries makes it possible to obtain uniformly distributed pores in adense ceramic matrix. Depending on the forming method—pressing, castingin a mold, tape casting, extrusion or injection molding—a material isobtained with a plane geometry, a tubular geometry or a geometry of morecomplex shape.

Several embodiments of this technique of incorporating pore-formingparticles into a ceramic suspension are disclosed in United Statespatents published under the numbers U.S. Pat. No. 4,777,153, U.S. Pat.No. 4,883,497, U.S. Pat. No. 5,762,737, U.S. Pat. No. 5,846,664 and U.S.Pat. No. 5,902,429 and in the publications by Lyckfeldt et al. and Aptéet al. (O. Lyckfeldt, E. Lidén, R. Carlsson, “Processing of thermalinsulation materials with controlled porosity”, Low expansion materials,pp 217-229; S. F. Corbin, P. S. Apté, J. Am. Ceram. Soc., 82, 7, 1999,pp 1693-1701). Apté et al. describe in particular a method using thetape casting of ceramic suspensions containing pore-forming particlesand the thermocompression of tapes in order to obtain, after sintering,a porous material with a discrete porosity gradient.

The pore former may also be a preform impregnated with a ceramicsuspension (ceramic powder+solvent+organic additives).

The infiltration of polymer foams by a ceramic suspension is used toobtain bulk ceramics having a substantial open porosity. In this case,the total porosity is directly due to the structure of the foam, butthis technique does not allow micron pore sizes to be achieved andcannot be used to prepare thin materials.

U.S. Pat. No. 4,780,437 discloses a method for preparing thin porousmaterials by infiltration of a flocking of pyrolyzable pore-formingfibers by a ceramic suspension. The materials obtained by this methodhave oriented anisotropic pores.

Controlling the structure, whether as a dense system or a porous systemwith a porosity gradient, and controlling the microstructure, especiallythe particle size distribution and the pore size distribution of aceramic article, is a key factor as regards its intrinsic properties andas regards its applications in terms of performance, reproducibility,lifetime and cost.

At the present time, it is not known how to manufacture a thin ceramicmembrane, having a thickness of a few hundred microns, possessing acontinuous controlled surface porosity gradient ranging from 0% (denseceramic) to about 80% (highly porous system) in a single operation. Allthe articles produced using the various known methods have discrete ordiscontinuous controlled porosity gradients. Now, the presence, even inthe same material, of these discrete porosity gradients may cause, atthe various interfaces, layer debonding and delamination phenomena,especially because of the differences in thermal expansion coefficientsbetween these regions. This results in rapid degradation of the article.

The fact of being able to produce a continuous controlled surfaceporosity gradient in a material should prevent the succession ofinterfaces between the layers of different porosity and consequentlyavoid these degradation phenomena.

In the production of electrochemical cells formed from a densesolid-state electrolyte and electrodes, called volume electrodes, suchas those described in international patent application WO 95/32050, thefact of controlling a microstructure of the solid-state electrolyte witha continuous controlled surface porosity gradient completely or partlyfilled with an electrode material should make it possible:

-   -   to promote physical compatibility and chemical compatibility        between volume electrode and dense solid-state electrolyte and        thus improve the cohesion of the interface between these two        materials;    -   to limit the energy costs associated with interfacial        overpotentials; and    -   to promote the diffusion, disassociation and recombination of        oxygen throughout the three-dimensional edifice of the volume        electrode/dense solid-state electrolyte porous structure, by        uniformly delocalizing volumewise the electrode reaction.

The electrochemical cells thus formed have improved performance in termsof electrochemical performance (current density applied per unit area),lifetime, aging (degradation) and energy cost.

In the case of the production of solid-state fuel cells or SOFCs (solidoxide fuel cells), these are formed from a dense solid-state electrolyteof small thickness (between 5 μm and 300 μm, preferably between 10 μmand 100 μm) deposited either on the anode electrode (fuel side) or onthe cathode electrode (air side). The fact of controlling a solid-stateelectrolyte structure/microstructure (thickness, density, particle size,porosity with a continuous compositional gradient created by total orpartial filling of a continuous controlled surface porosity gradient ofone of the “support” electrode (anode or cathode) materials should makeit possible:

-   -   to promote physical compatibility and chemical compatibility        between said anode (fuel) or cathode (air) “support” electrode        and the dense solid-state electrolyte and thus improve the        cohesion of the interface between these two materials;    -   to limit the energy costs associated with interfacial        overpotentials and with the thickness of the solid-state        electrolyte; and    -   to promote the diffusion, dissociation and recombination of        oxygen throughout the three-dimensional edifice of the “anode or        cathode” volume electrode/dense solid-state electrolyte porous        structure by uniformly delocalizing volumewise the electrode        reaction.

The solid-state fuel cell elements thus formed have improved performancein terms of productivity (higher power produced per unit area), loweredoperating temperature, lifetime, aging (degradation) and energy cost.

In the case of the production of a catalytic membrane ceramic reactorfor the reaction for example, of reforming methane into a syngasaccording to the chemical reaction CH₄+½O₂→2H₂+CO, the dense membrane isa material having a crystal structure of the ABO₃, AA′BB′O₆ (A,A′:lanthanide and/or actinide; B,B′: transition metal), brown-milleriteand/or pyrochlore perovskite type. The material possesses mixedconductivity properties and is deposited in the form of a dense membrane(density>94%) with a thickness of between 5 μm and 500 μm, preferablybetween 10 μm and 300 μm, on a porous support of the same chemicalcomposition or of a different chemical composition. The fact ofcontrolling a structure/microstructure (thickness, density, particlesize, residual porosity) of the dense (mixed conducting) membrane with acontinuous compositional gradient by total or partial filling of acontinuous controlled surface porosity gradient of the support shouldmake it possible:

-   -   to promote physical compatibility and chemical compatibility        between said porous support and the dense mixed conducting        membrane and thus improve the cohesion of the interface between        these two materials;    -   to increase the flux of oxygen produced, this flux being,        according to Wagner's law, inversely proportional, for a given        working range, to the thickness of the dense membrane;    -   to promote the diffusion, dissociation and recombination of        oxygen throughout the three-dimensional edifice of the porous        structure of the support if the latter is of the same chemical        composition as the membrane; and    -   to improve the mechanical integrity of the membrane reactor        essentially by virtue of the mechanical properties of the        support.

The mixed conducting ceramic membrane for the methane reforming reactionshould show improved performance in terms of oxygen flux per unit area,lowering of the working temperature, lifetime, aging (degradation) andmechanical integrity in a reducing medium compared with a self-supportedsystem.

In this application—reforming—a catalyst is deposited on the surface ofa thin dense membrane that may or may not have a developed surface andsurface roughness, said membrane being supported on a porous support ofthe same nature or of a different chemical nature.

SUMMARY OF THE INVENTION

This is why the subject of the invention is a method for preparing athin solid-state composition, essentially formed from a ceramic and/ormetallic material (A) having, within said composition, a surfaceconcentration gradient of a ceramic and/or metallic material (B) ofchemical composition identical to or different from that of material(A), characterized in that it comprises the following successive steps:

-   -   a step (1) of infiltrating a porous pore-forming substrate of        controlled thickness with a suspension of a material (A) in a        solvent;    -   a step (2) of solvent evaporation, in order to form a pore        former/material (A) composite structure;    -   a debinding step (3);    -   a sintering or presintering step (4);    -   a step (5) of total or partial filling of the porosity created        on the surface of material (A) by material (B) or a precursor of        said material (B), as the case may be and if desired;    -   a step (5′) of heat treatment; and in all cases    -   a step (6) of sintering or cosintering the assembly obtained in        either of steps (5) and (5′).

BRIEF DESCRIPTION OF THE DRAWINGS

For a further understanding of the nature and objects for the presentinvention, reference should be made to the following detaileddescription, taken in conjunction with the accompanying drawings, inwhich like elements are given the same or analogous reference numbersand wherein:

FIG. 1 illustrates the various steps of the method for producing aceramic membrane formed mainly from a thin material (A) having a surfaceconcentration gradient of a material (B).

FIG. 2 illustrates the method of preparing a ceramic membrane mainlyformed from a thin material (A) having a surface concentration gradientof a material (B).

FIG. 3 is a photograph obtained by scanning electron microscopy of thesurface of a porous pore-forming substrate.

FIG. 4 is a collection of various photographs obtained by scanningelectron microscopy of polished sections of sintered material (A)obtained by infiltration of a porous pore-forming substrate by a BICOVOX10 suspension (material (A)).

FIG. 5 is a photograph obtained by scanning electron microscopy of apolished section of the interface between two ceramic materials A and B,BICOVOX 10 (A) and a material (B) of perovskite structure, respectively.

FIG. 6 illustrates the manufacture of porous/dense/porous multilayerelements by thermocompression, in the green state, of a stack of twoback-to-back tapes of a material (A), which tapes are produced by themethod of infiltrating a porous pore-forming substrate with a suspensionof ceramic material A.

DESCRIPTION OF PREFERRED EMBODIMENTS

In the definition of the method forming the subject of the presentinvention, the term “thin” is generally understood to mean a totalthickness of between about 0.05 mm and about 5 mm and more particularlybetween about 0.25 mm and about 2 mm.

In the definition of the method forming the subject of the presentinvention, the expression “continuous controlled surface porositygradient” indicates that the porosity of said material varies from avalue tending toward 0%, at one of its faces (called the dense surface),to a value tending toward about 80% at its opposite face (called theporous face).

The term “surface porosity” is understood to mean the pores on thesurface of material (A) accessible either to a gas, liquid orsupercritical fluid, for example to a gas or a gas mixture such as airor natural gas, for the operation of a purely ionic or mixed conductingceramic membrane, or to a liquid such as a suspension or a molten metal,for an infiltration operation.

When the material is intended for the manufacture of a membrane allowingoxygen ions to pass through it, the porosity of the material at thedense face is around 0%. It is less than or equal to 80% and moreparticularly equal to about 60% at the porous face.

The expression “porous pore-forming substrate” denotes a porous stack ofsolid pore-forming particles or of a blend of solid pore-formingparticles, of the same or different size and/or shape and/or nature. Theporosity of the substrate is between about 20% and about 90% andpreferably greater than or equal to 30% and less than or equal to 70%,and more particularly approximately equal to 40%. The porosity of theporous pore-forming substrate corresponds to the interstices between thepore former or formers, whether these be particles, flakes or fibers.This interconnected stack porosity, also called open porosity, allowsinfiltration by the ceramic suspension.

The term “pore former” denotes any material capable of being removed, bythermal decomposition or etching during the debinding step prior tosintering, leaving pores in the material obtained after this step andwithout leaving residues. As pore formers, it is preferred to usepolymers existing in particulate form and in relatively isotropic formsuch as, for example, micronized polypropylene waxes (for example,PropylTex™270S or PropylTex™325S from MicroPowders, Inc.), polyamides(for example, ORGASOL™ from Elf Atochem), latexes,polytetrafluoroethylene or polystyrene spheres. As pore formers,cellulose fibers (for example ARBOCEL™BE600-10 from Rettenmeier),starches (for example standard corn starch, SP standard wheat starch orpotato starch from Roquette Frères, or REMYRISE™DR rice starch fromRémy) or graphite are also used.

The term “of material suspension (A)” indicates that the suspension hasa suitable viscosity and suitable rheological behavior for it toinfiltrate into the porous pore-forming substrate so as to induce acontinuous pore-filling gradient, ranging from 0% filling of the pores,at the face opposite the infiltration face, up to about 100% at theinfiltration face.

Step (1), the infiltration step, is carried out, for example, by thetechnique called tape casting. The tape casting technique is carried outby means of a casting bed. This technique is particularly appropriatewhen it is desired to obtain a ceramic material of planar shape. It isalso possible to use it to produce tubes by winding, for example arounda mandrel, dense ceramic sheets filled with pore-forming particles, orto produce corrugated structures by a forming or thermoforming operationon a preform.

The gradient of infiltration of the porous pore-forming substrate withthe suspension is obtained by controlling its viscosity and itsTheological behavior. Thus, increasing the proportion of organic phasein the suspension of pore-forming particles reduces the porosity of thesubstrate by closing up the interstices between the pore-formingentities and making it more difficult for the suspension of givenviscosity to infiltrate. Increasing the viscosity of the suspension alsomakes infiltration of the porous pore-forming substrate more difficult.

Step (2), the solvent evaporation step, is, if necessary, carried out bycirculation of a stream of hot air.

Step (3), the debinding step, consists in eliminating the pore formersand the various organic auxiliaries used to implement the above steps ofthe method by thermal decomposition or etching.

Step (4), the presintering or sintering step, consists of a heattreatment for consolidating and/or densifying material (A) around thepores developed by the pore former. During this heat treatment thermallyactivated diffusion phenomena are responsible for the transportation ofmaterial and, consequently, the consolidation of the structure and thedensification of the material. The sintering generally consists of aheat treatment at an optimum temperature.

The term “optimum sintering temperature” denotes the temperature, belowthe melting point or decomposition temperature of the material, forwhich densification is at a maximum and grain growth is limited. In thecase of materials of the family of BIMEVOX compounds, the sinteringtemperature is between 700 and 850° C. and a mean particle size aftersintering of less than 5 μm and preferably less than 3 μm will bepreferred.

A presintering operation consists of a simple consolidation of thematerial, either without densification or with a slight densification,at a temperature below the sintering temperature of the material. Thepurpose of the consolidation is to ensure cohesion during the subsequentstep of filling the pores of material (A).

Steps (3) and (4) may be carried out during one and the same operationas a single step (3′) called the debinding-presintering ordebinding-sintering step.

Step (5), of total or partial filling of the porosity created on thesurface of material (A) by a material (B) or precursor of said material(B), may be carried out by infiltration or by impregnation with a liquidcontaining material (B) or a precursor of said material (B), by chemicalvapor deposition (CVD) of a gas containing material (B) or itsprecursor, or by deposition, in a supercritical phase, of a fluidcontaining material (B) or its precursor.

The expression “precursor of material B” is understood to mean acompound (an organic molecule, an organometallic, a salt, etc.) allowingmaterial (B) to be obtained after a heat treatment.

Step (5), of total or partial filling of the pores, may include theevaporation of a solvent.

Step (6), of sintering or cosintering the material (A)/material (B)combination, consists of a heat treatment for consolidating anddensifying material (B), or even of densifying the presintered material(A). This step may also allow a precursor of material (B) to decomposein order to form material (B).

In all cases, this heat treatment is carried out at a temperature lessthan or equal to the sintering temperature of material (A). This stepalso makes it possible to achieve good cohesion of the interface betweenmaterial (A) and material (B). This step may also include a debindingoperation, by thermal decomposition or etching, in order to remove thevarious organic auxiliaries used for the total or partial filling of thepores created on the surface of material (A) by material (B) or aprecursor of said material (B).

According to a first variant of the method as defined above, thecomposite structure (S) resulting from step (2) undergoes a step (2′) ofcutting into structure elements (s). The elements (s) obtained arepreferably of identical shape and size.

When it is desired to produce either a solid-state electrolyte or asupported mixed conducting membrane, two elements (₁) and S₂) obtainedin step 2′) may be stacked back-to-back, their dense faces beingadjacent, in order to form an assembly (H), which then undergoesthermocompression followed by steps (3) and (4), or by step (3′), thenby steps (5) and (6) of the method as defined above.

In this case, the dimensions of the die for thermocompression of theassembly (H) may be tailored to the dimensions of the elements s, (s₁)and s₂).

The thermocompression operation carried out on the assembly (H)generally consists of pressing the latter under a pressure of about 50MPa for 5 to 10 minutes at a temperature above the glass transitiontemperature (T_(g)) of the organic phase used, which comprises thebinder and the plasticizer. It is generally below 100° C.

According to a first particular aspect of the method forming the subjectof the present invention, this comprises a prior step (P) of preparingthe porous pore-forming substrate. This preparation more particularlycomprises:

-   -   a step (P_(a)) of preparing a suspension of one or more solid        pore formers in a solvent, if necessary in the presence of        binders, plasticizers and/or dispersants, and with, if so        desired, the addition, in a small proportion, of ceramic and/or        metallic particles or of precursors of a ceramic and/or metallic        material to said suspension;    -   a step (P_(b)) of casting said suspension formed in step (P_(a))        on a flat surface; and    -   a step (P_(c)) of evaporating said solvent.

As solvent, a liquid may be chosen that is inert with respect to thepore formers and especially a liquid in which the pore formers areinsoluble.

This is in general an organic solvent, for example methanol, ethanol,isopropanol, butanol, methyl ethyl ketone (MEK), an ethanol+MEK mixtureor trichloroethylene.

As dispersant, a compound or a blend of compounds is chosen whichresults in the electrostatic and/or stearic repulsion of the poreformers, whether they be particles, fibers or flakes, in the solvent. Itis preferable to choose a compound or a blend of compounds from thefamily of phosphoric esters, such as BEYCOSTAT™A259, or fluoroalkylesters or alkyl ethoxylates.

As binder, a compound or a blend of compounds is chosen that ischemically compatible with the other constituents of the suspension andof the ceramic material optionally present. Preferably, a compoundhaving a low glass transition temperature T_(g) is chosen. Moreparticularly, a compound soluble in the chosen solvent is chosen. Amongcompounds or blends of compounds commercially available, there arepolyacrylics such as DEGALAN™ or polyvinyls such as polyvinyl butyrals.

As plasticizer, a commercially available compound or blend of compounds,which is known to possess this property, is chosen, such as phthalates,such as dibutyl phthalate or butyl phthalate or benzyl phthalate, orelse polyethylene glycols. More particularly, a compound soluble in thechosen solvent is chosen.

As casting support, it is general practice to use a glass surface, astainless steel or a plastic film such as, for example, a Mylar™ film ora polypropylene film.

Adding a binding agent and/or a plasticizing agent, in a smallproportion, to the pore-former suspension makes it possible to obtain aporous polymer substrate that is flexible and able to be handled aftersolvent evaporation and that does not deteriorate during infiltration ofthe suspension of material (A). These compounds form bridging betweenthe pore formers.

In general, the constituents of the suspension prepared in step (P_(a))are chosen so that, after evaporation of the solvent, the pore-formingsubstrate formed does not adhere to the support on which the casting ofsaid suspension is carried out and so that it does not crack.

If necessary, step (P_(b)) is preceded by a step (P_(d)) ofdeagglomerating the pore-forming particles in said suspension formed instep (P_(a)), said step (P_(d)) being optionally followed by a step(P_(e)) of deaerating said suspension.

Step (P_(d)) generally consists of breaking up the agglomerates bymechanical action, such as grinding, for example by attrition, or withultrasound.

Step (P_(e)) generally consists of eliminating the air bubbles presentin the suspension, for example by applying a vacuum, by rotating it in ajar or by screening.

Step (P_(b)) is carried out using the technique called tape casting.This technique is particularly appropriate when it is desired to obtaina ceramic material of thin planar shape. It may also be used to producetubes by winding, for example around a mandrel, dense ceramic sheetsfilled with pore-forming particles, or to produce shaped, for examplecorrugated, structures by a forming or thermoforming operation on apreform.

The tape casting technique is carried out using a casting bed. Such adevice is commercially available.

According to a second particular aspect of the method forming thesubject of the present invention, this comprises a prior step (Q) ofpreparing a suspension of material (A) in a solvent optionally with theaddition of pore-forming particles.

This preparation more particularly comprises:

-   -   a step (Q_(a)) of preparing a suspension of particles of        material (A) and optionally of pore-forming particles in a        solvent, in the presence of a dispersant; and    -   a step (Q_(b)) of adding a binder and a plasticizer and        optionally a wetting agent to the suspension prepared in step        (Q_(a)).

As solvent, a liquid is chosen that makes it possible to dissolve theorganic auxiliaries used, such as the dispersants, binders orplasticizers. This is in general an organic solvent, for examplemethanol, ethanol, isopropanol, butanol, methyl ethyl ketone (MEK), anethanol+MEK mixture or trichloroethylene.

As dispersant, a compound or a blend of compounds is chosen that ischemically compatible with the other constituents of the suspension andof the material (A). It is preferable to choose a compound or a blend ofcompounds from the family of phosphoric esters, such as BEYCOSTAT™A259,or fluoroalkyl esters or alkyl ethoxylates.

As binder, a compound or a blend of compounds is chosen that ischemically compatible with the other constituents of the suspension andof the material (A). Preferably, a compound having a low glasstransition temperature T_(g) is chosen. More particularly, a compoundsoluble in the chosen solvent is chosen. Among compounds or blends ofcompounds commercially available, there are polyacrylics such asDEGALAN™ or polyvinyls such as polyvinyl butyrals.

As plasticizer, a commercially available compound or blend of compounds,which is known to possess this property, is chosen, such as phthalates,such as dibutyl phthalate or butyl phthatate or benzyl phthalate, orelse polyethylene glycols. More particularly, a compound soluble in thechosen solvent is chosen.

As wetting agent, a commercially available compound or blend ofcompounds, which is known to possess this property, is chosen, such asfluoroalkyl polymers.

This preparation may include a step (Q_(c)) of deagglomerating thesuspension formed at step (Q_(a)) before it is subjected to step(Q_(b)).

Step (Q_(c)) generally consists in breaking up the aggregates bymechanical action, such as grinding, for example by attrition or byultrasound.

For correct implementation of the method forming the subject of thepresent invention, it is preferable for the powder of material (A), ofwhich the suspension is prepared in step (Q_(a)), to consist ofparticles of equiaxed shape with a narrow size distribution centeredaround a mean value of between 0.1 μm and 10 μm, preferably between 0.2μm and 1 μm.

This preparation may also include a step (Q_(d)) of deaerating thesuspension obtained in step (Q_(b)).

Step (Q_(d)) generally consists in removing the air bubbles present inthe suspension, for example by applying a vacuum, by rotation in a jaror by screening.

According to a third particular aspect of the method forming the subjectof the present invention, this comprises a prior step (R) of preparing asuspension of material (B) or of a precursor of said material (B), in asolvent, optionally with the addition of pore-forming particles.

This preparation more particularly comprises:

-   -   a step (R_(a)) of preparing a suspension of solid particles in a        solvent, in the presence of a dispersant; and    -   a step (R_(b)) of adding, to the suspension prepared in step        (R_(a)), a binder and a plasticizer and optionally a wetting        agent.

As solvent, a liquid is chosen that makes it possible to dissolve theorganic auxiliaries used, such as the dispersants, binders orplasticizers. This is in general an organic solvent, for examplemethanol, ethanol, isopropanol, butanol, methyl ethyl ketone (MEK), anethanol+MEK mixture or trichloroethylene.

As dispersant, a compound or a blend of compounds is chosen that ischemically compatible with the other constituents of the suspension andof the material (B) ot its precursors.

It is preferable to choose a compound or a blend of compounds from thefamily of phosphoric esters, such as BEYCOSTAT™A259, or fluoroalkylesters or alkyl ethoxylates.

As binder, a compound or a blend of compounds is chosen that ischemically compatible with the other constituents of the suspension andof the material (B). Preferably, a compound having a low glasstransition temperature T_(g) is chosen. More particularly, a compoundsoluble in the chosen solvent is chosen. Among compounds or blends ofcompounds commercially available, there are polyacrylics such asDEGALAN™ or polyvinyls such as polyvinyl butyrals.

As plasticizer, a commercially available compound or blend of compounds,which is known to possess this property, is chosen, such as phthalates,such as dibutyl phthalate or butyl phtalate or benzyl phthalate, or elsepolyethylene glycols. More particularly, a compound soluble in thechosen solvent is chosen.

As wetting agent, a commerically available compound or blend ofcompounds, which is known to possess this property, is chosen, such asfluoiroaltyl polymers.

This preparation may include a step (R_(c)) of deagglomerating thesuspension prepared in step (R_(a)) before it is subjected to step(R_(b))

This deagglomeration step generally consists in breaking up theagglomerates by mechanical action, such as grinding, for example byattrition or by ultrasound.

For correct implementation of the method forming the subject of thepresent invention, it is preferable for material (B) or its precursor,the suspension of which was prepared in step (R_(a)), to consist of apowder and more particularly of a powder of particles of equiaxed shape,with a narrow size distribution centered around a mean value of between0.1 μm and 10 μm, preferably between 0.2 μm and 1 μm.

This preparation may also include a step (R_(a)) of deaerating thesuspension resulting from step (R_(b)).

According to a fourth particular aspect of the method forming thesubject of the present invention, materials (A) and (B), of identical ordifferent compositions used, are metallic materials. The method thusused therefore makes it possible to obtain more particularly metal formsof high quality.

The metallic materials are mainly noble metals, such as platinum,palldium, gold or rhodium, or transition metals, such as for examplenickel, chromium, manganese, tungsten, vanadium or niobium. They also bemetal alloys.

According to a fifth particular aspect of the method forming the subjectof the present invention, at least one of materials (A) and (B), ofidentical or different chemical compositions, is chosen from dopedceramic oxides which, at the operating temperature, are in the form of acrystal lattice having oxide ion vacancies, and more particularly in theform of a cubic phase, fluorite phase, Aurivillius-type perovskitephase, brown-millerite phase or pyrochlore phase. Among these there are:

-   -   (a)—oxides of formula (I):        (M_(a)O_(b))_(1-x)(R_(c)O_(d))_(x)  (I)        in which M represents at least one trivalent or tetravalent atom        chosen mainly from bismuth (Bi), cerium (Ce), zirconium (Zr),        thorium (Th), gallium (Ga) or hafnium (Hf), a and b are such        that the M_(a)O_(b) structure is electrically neutral, R        represents at least one divalent or trivalent atom chosen mainly        from magnesium (Mg), calcium (Ca) or barium (Ba), strontium        (Sr), gadolinium (Gd), scandium (Sc), ytterbium (Yb), yttrium        (Y), samarium (Sm), erbium (Er), indium (In), niobium (Nb) or        lanthanum (La), c and d are such that the R_(c)O_(d) structure        is electrically neutral and x is generally between 0.05 and 0.30        and more particularly between 0.075 and 0.15.

As examples of oxides of formula (I), there are stabilized zirconias,gallates or cerium oxides, such as:

-   -   stabilized zirconia of formula (Ia):        (ZrO₂)_(1-x)(Y₂O₃)_(x)  (Ia)        in which x is between 0.05 and 0.15;    -   (b)—perovskite materials of formula (II):        [Ma_(1-x)Ma′_(x)][Mb_(1-y)Mb′_(y)]O_(3-w)  (II)        in which Ma and Ma′, which are identical or different, are        chosen from the families of alkaline-earth metals, lanthanides        and actinides and more particularly from La, Ce, Pr, Nd, Pm, Sm,        Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, Y or Mg, Ca, Sr or Ba, Mb        and Mb′, which are identical or different, represent one or more        atoms chosen from the transition metals, and more particularly        from Sc, Ti, V, Cr, Mn, Fe, Co, Ni, Cu, Zn or Ga, x and y, which        are identical or different, are greater than or equal to 0 and        less than or equal to 1 and w is such that the structure in        question is electrically neutral.

As examples of oxides of formula (II), there are lanthanum nickel oxide(LaNiO₃), calcium lanthanum manganites (Ca_(u)La_(v)MnO_(w)), lanthanumstrontium manganites (La_(u)Sr_(v)MnO_(w)), lanthanum strontiumcobaltites (La_(u)Sr_(v)CoO_(w)), lanthanum calcium cobaltites(Ca_(u)La_(v)CoO_(w)), gadolinium strontium cobaltites(Gd_(u)Sr_(y)CoO_(w)), lanthanum strontium chromites(La_(u)Sr_(v)CrO_(w)), lanthanum strontium ferrites(La_(u)Sr_(v)FeO_(w)) lanthanum strontium doped ferrites—transitionmetal (La_(u)Sr_(v)Fe_(c)Mb′dO_(w)) lanthanum strontium ferrocobaltites(La_(u)Sr_(v)Co_(d)Fe_(c)O_(w)), for which compounds the sums u+v andc+d are equal to 1, and w is such that the structure in question iselectrically neutral. There is more particularly a compound of formula(IIa):La_(0.6)Sr_(0.4)Co_(0.8)Fe_(0.2)O_(w)  (IIa),in which w is such that the structure of formula (IIa) is electricallyneutral.

-   -   (c)—materials of the brown-millerite family of formula (III):        [Mc_(2-x)Mc′_(x)][Md_(2-y)Md′_(y)]O_(6-w)  (III)        in which, Mc represents a metal or a mixture of metals of the        family of alkaline-earth (Mg, Ca, Sr or Ba) compounds; Mc′        represents a metal or a mixture of metals of the family of        lanthanides and actinides and more particularly from La, Ce, Pr,        Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu or Y; Md        represents a metal or a mixture of metals of the family of 3d        transition metals and metals of group 13; and Md′ represents a        metal or a mixture of metals of the family of 3d transition        metals, metals of group 13 or metals of the family of        lanthanides or actinides, x and y are greater than or equal to 0        and less than or equal to 2, and w is such that the structure in        question is electrically neutral. Among metals of group 13,        aluminum (Al), gallium (Ga) or indium (In) are preferred for Md        and Md′.

Among transition metals, cobalt (Co), titanium (Ti), vanadium (V),chromium (Cr), manganese (Mn), zinc (Zn), nickel (Ni) or iron (Fe) areprepared for Md and Md′.

As compounds of formula (III), there are more particularly compounds offormula (IIIa):[Mc_(2-x)La_(x)][Md_(2-y)Fe_(y)]O_(6-w)  (IIIa)compounds of formula (IIIb):[Sr_(2-x)La_(x)][Ga_(2-y)Md′_(y)]O_(6-w)  (IIIb)and more particularly compounds of formula (IIIc):[Sr_(2-x)La_(x)][Ga_(2-y)Fe_(y)]O_(6-w)  (IIIc),such as, for example,Sr_(1.4)La_(0.6)GaFeO_(5.3),Sr_(1.6)La_(0.4)Ga_(1.2)Fe_(0.8)O_(5.3),Sr_(1.6)La_(0.4)GaFeO_(5.2),Sr_(1.6)La_(0.4)Ga_(0.8)Fe_(1.2)O_(5.2),Sr_(1.6)La_(0.4)Ga_(0.6)Fe_(1.4)O_(5.2),Sr_(1.6)La_(0.4)Ga_(0.4)Fe_(1.6)O_(5.2),Sr_(1.6)La_(0.4)Ga_(0.2)Fe_(1.8)O_(5.2),Sr_(1.6)La_(0.4)Fe₂O_(5.2),Sr_(1.7)La_(0.3)GaFeO_(5.15),Sr_(1.7)La_(0.3)Ga_(0.8)Fe_(1.2)O_(5.15),Sr_(1.7)La_(0.3)Ga_(0.6)Fe_(1.4)O_(5.15),Sr_(1.7)La_(0.3)Ga_(0.4)Fe_(1.6)O_(5.15),Sr_(1.7)La_(0.3)Ga_(0.2)Fe_(1.8)O_(5.15),Sr_(1.8)La_(0.2)GaFeO_(5.1),Sr_(1.8)La_(0.2)Ga_(0.4)Fe_(1.6)O_(5.1)and Sr_(1.8)La_(0.2)Ga_(0.2)Fe_(1.8)O_(5.1).

-   -   (d)—compounds of the BIMEVOX family of formula (IV):        (Bi_(2-x)M_(x)O₂)(V_(1-y)M′_(y)O_(z))  (IV)        in which M represents one or more metals substituting for        bismuth, chosen from those having an oxidation number of less        than or equal to 3, M′ represents one or more elements        substituting for vanadium, chosen from those having an oxidation        number of less than or equal to 5, the limiting values of x, y,        and therefore z, being dependent on the nature of the        substitution elements M and M′. As examples of oxides of formula        (IV), there are:    -   compounds of formula (IVa):        (Bi₂O₂)(V_(1-y)M′_(y)O_(z))  (IVa)        corresponding to formula (IV) in which x is equal to 0 and y is        different from 0 and M′ is advantageously selected from alkali        metals, alkaline-earth metals, transition metals or elements        from Groups III to V of the Periodic Table, or from rare earths.

When M′ represents a transition metal, it is more particularly zinc(Zn), copper (Cu), nickel (Ni), cobalt (Co), iron (Fe), manganese (Mn)or cadmium (Cd).

When M′ is an alkaline-earth metal, it is especially calcium (Ca),strontium (Sr) or barium (Ba).

However, M′ may also represent a metal having an oxidation number equalto 3, such as antimoine (Sb), indium (In) or aluminum (Al), a metalhaving an oxidation number equal to 4, such as titanium (Ti), tin (Sn)or ruthenium (Ru), or a substitution element having an oxidation numberequal to 5, such as niobium (Nb), tantalum (Ta) or phosphorus (P).

M′ may also represent an alkali metal such as sodium (Na) or mayrepresent lead (P_(b)) in oxidation state 2.

As examples of compounds of formula (IVa), there are more particularlyBi₂V_(0.9)Co_(0.1)O_(5.35) (called BICOVOX 10) orBi₂V_(0.9)Cu_(0.1)O_(5.35) (called BICUVOX 10);

-   -   compounds of formula (IVb):        (Bi_(2-x)M_(x)O₂)(VO_(z))  (IVb)        corresponding to formula (IV) in which y is equal to 0 and x is        different from 0, M is as defined above and is more particularly        chosen from rare earths such as lanthanum.

Mention may also be made among compounds of formula (IV) of those inwhich the oxygen atom is partially substituted with fluorine, or elsethose having mixed bismuth and vanadium substitutions. As compositionsof this type, there are, for example, compounds of formula (IVc):(Bi_(2-x)Pb_(x)O₂)(V_(1-y)Mo_(y)O_(z)).

In general, when the ceramic material used is a powder of a compoundfrom the perovskite, brown-millerite family pyrochlor or BIMEVOX, themean particle size is between 0.2 and 50 microns.

According to one particular embodiment of the present invention, the twomaterials are chosen from doped ceramic oxides as defined above and mostparticularly from compounds of formulae (I), (II), (III), (Ia), (IIa),(IIIa), (IIIb) or (IIIc) as defined above.

According to another particular embodiment of the present invention,materials A and B have different chemical compositions. In this case, atthe use temperature, they are in the form of crystal lattices which areeither identical or different.

According to another particular embodiment of the present invention,materials (A) and (B) have the same chemical composition. The solidcomposition resulting from the method described in the present patentapplication is distinguished from those of the prior art by itsdifferent microstructure, this being characteristic of the method used.

The subject of the invention is also a method and its variant such asthose defined above, characterized in that material (B) is chosen fromcarbides or nitrides such as silicon carbide SiC or silicon nitrideSi₃N₄, SiAlON, alumina Al₂O₃, aluminum silicates or their derivativessuch as mullite (2SiO₂.3Al₂O₃) or cordierite (Mg₂Al₄Si₅O₁₈), magnesia(MgO), calcium phosphates and its derivatives such as hydroxyapatite[Ca₄(CaF)(PO₄)₃], tricalcium phosphate [Ca₃(PO₄)₂] and undoped ceramicoxides such as zirconia (ZrO₂) or ceria (CeO₂).

The method as described above is, for example, used to prepare amembrane formed from a porous material (B) supporting a dense mixedconducting ceramic material (A) of different chemical composition.

According to another aspect of the present invention, this relates to aceramic and/or metallic material obtained by the method as defined aboveand to a solid-state electrolyte or a mixed ionic/electronic conductor,these being obtained by the variant of said method as defined above.

The subject of the invention is also an electrochemical cell comprisingthe solid-state electrolyte, as defined above, and a mixedionically/electronically conducting ceramic membrane comprising a mixedionic/electronic conductor as defined above.

The subject of the invention is also an ionic/electronic mixedconducting ceramic membrane comprising a material (A) chosen from:

-   -   (i)—oxides of formula (I):        (M_(a)O_(b))_(1-x)(R_(c)O_(d))_(x)  (I),        in which M represents at least one trivalent or tetravalent atom        mainly chosen from bismuth (Bi), cerium (Ce), zirconium (Zr),        thorium (Th), gallium (Ga) or hafnium (Hf), a and b are such        that the structure M_(a)O_(b) is electrically neutral, R        represents at least one divalent or trivalent atom mainly chosen        from magnesium (Mg), calcium (Ca) or barium (Ba), strontium        (Sr), gadolinium (Gd), scandium (Sc), ytterbium (Yb), yttrium        (Y), samarium (Sm), erbium (Er), indium (In), niobium (Nb) or        lanthanum (La), c and d are such that the structure R_(c)O_(d)        is electrically neutral and x is generally between 0.05 and 0.30        and more particularly between 0.075 and 0.15, and more        particularly stabilized zirconias of formula (Ia):        (ZrO₂)_(1-x)(Y₂O₃)_(x)  (Ia)        in which x is between 0.05 and 0.15;    -   (ii)—perovskite materials of formula (II):        [Ma_(1-x)Ma′_(x)][Mb_(1-y)Mb′_(y)]O_(3-w)  (II)        in which Ma and Ma′, which are identical or different, are        chosen from the alkaline-earth, lanthanide and actinide        families, and more particularly from La, Ce, Pr, Nd, Pm, Sm, Eu,        Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, Y, or Mg, Ca, Sr or Ba; Mb and        Mb′ which are identical or different, represent one or more        atoms chosen from transition metals, and more particularly from        Sc, Ti, V, Cr, Mn, Fe, Co, Ni, Cu, Zn or Ga; x and y, which are        identical or different, are greater than or equal to 0 and less        than or equal to 1; and w is such that the structure in question        is electrically neutral, and more particularly compounds of        formula (IIa):        La_(0.8)Sr_(0.4)Co_(0.8)Fe_(0.2)O_(w)  (IIa),        in which w is such that the structure of formula (IIa) is        electrically neutral, or:    -   (iii)—materials of the brown-millerite family of formula (III):        [Mc_(2-x)Mc′_(x)][Md_(2-y)Md′_(y)]O_(6-w)  (III)        in which, Mc represents a metal or a mixture of metals of the        family of alkaline-earth (Mg, Ca, Sr or Ba) compounds; Mc′        represents a metal or a mixture of metals of the family of        lanthanides and actinides and more particularly from La, Ce, Pr,        Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu or Y; Md        represents a metal or a mixture of metals of the family of 3d        transition metals or metals of group 13; and Md′ represents a        metal or a mixture of metals of the family of 3d transition        metals, metals of group 13, lanthanides or actinides; x and y,        which are identical or different, are greater than or equal to 0        and less than or equal to 2; and w is such that the structure in        question is electrically neutral and more particularly materials        of formula (IIIa):        [Mc_(2-x)La_(x)][Md_(2-y)Fe_(y)]O_(6-w)  (IIIa),        or of formula (IIIb):        [Sr_(2-x)La_(x)][Ga_(2-y)Md′_(y)]O_(6-w)  (IIIb)        or of formula (IIIc):        [Sr_(2-x)La_(x)][Ga_(2-y)Fe_(y)]O_(6-w)  (IIIc)        and constituting a dense phase supported by a material (B)        chosen from carbides or nitrides such as silicon carbide SiC or        silicon nitride Si₃N₄, alumina Al₂O₃, aluminum silicates or        their derivatives such as mullite (2SiO₂.3Al₂O₃) or cordierite        (Mg₂Al₄Si₅O₁₈), magnesia (MgO), calcium phosphates and their        derivatives such as hydroxyapatite [Ca₄(CaF) (PO₄)₃], tricalcium        phosphate [Ca₃(PO₄)₂] and undoped ceramic oxides such as        zirconia (ZrO₂) or ceria (CeO₂) and constituting a porous        support.

This membrane is preferably prepared by the method as defined above.

The membrane as defined above may furthermore include a reformingcatalyst applied to the external face of the dense phase of material(A).

According to another aspect of the present invention, this relates tothe use of the solid-state electrolyte obtained by the variant of themethod as defined above, to extract oxygen from a gaseous mixturecontaining it or to analyze the presence of oxygen in a gaseousatmosphere. Mention may be made in particular of the use of thesolid-state electrolyte obtained by the variant of the method as definedabove either to produce ultrapure oxygen in a vacuum or not or, inapplications requiring oxygen-free atmospheres or atmospheres having alow oxygen content, such as the electronic components industry or thefood industry, to remove oxygen from said atmosphere or to reduce theoxygen content, said gaseous atmosphere being above a solid or a liquid.

This is why the subject of the invention is also a method for producingultrapure oxygen, consisting in separating oxygen from air by ionicconduction through an electrochemical cell as defined above and a methodfor reducing or even eliminating oxygen from a gaseous atmosphere inwhich applications requiring oxygen-free atmospheres or atmosphereshaving a low oxygen content are carried out, consisting in separatingoxygen from said atmosphere by ionic conduction through anelectrochemical cell as defined above.

It is also possible to use an ionic conducting ceramic membrane asdefined above to produce oxygen which is used directly in a chemicalreaction, especially with hydrogen in order to produce electricalenergy, for example, in a solid-state fuel cell of the SOFC type.

This is why the subject of the invention is also a method for producingthermal and electrical energy within a solid-state fuel cell, by thereaction of oxygen with hydrogen, characterized in that said oxygen isobtained by separating it from air, by ionic conduction through aceramic membrane and more particularly through a supported ceramicmembrane, either on the anode (fuel side) or on the cathode (air side),as defined above.

According to another aspect of the present invention, this relates tothe use of a mixed conducting ceramic membrane, supported on a poroussupport having a chemical composition identical to or different from thedense membrane, as a catalytic membrane reactor in a method forproducing syngas by the catalytic reaction of natural gas optionallywith steam and oxygen, characterized in that said oxygen is obtained byseparating it from air, by mixed ionic/electronic conduction through thedense ceramic membrane as defined above.

Another subject of the invention is the use of the article describedabove in a method for producing ultrapure oxygen, characterized in thatsaid oxygen is separated from air by mixed ionic/electronic conductionthrough a supported ceramic membrane as defined above.

Another subject of the invention is the use of a supported ceramicmembrane as defined above in an industrial process for synthesizing anorganic compound from hydrocarbon-based molecules, comprising at leastone oxidation step, catalytic or non-catalytic, using gaseous oxygen,characterized in that said oxygen is obtained by separating it from air,by mixed ionic/electronic conduction through a ceramic membrane asdefined above.

In all situations of the membrane catalytic reactor, a catalystcorresponding to the expected catalytic reaction, for example areforming reaction or a provided oxidation reaction, is, eitherdispersed on the surface of the supported dense thin membrane ordeposited in powder form or extruded in direct contact with the membranesystem.

Finally, the subject of the invention is the use of a compositionobtained by the method as defined above, in order to produce filtermembranes for gases or liquids, ceramic-to-metal seals, biomaterials orsensors. In this composition formed from three phases—material (A),material (B) and pores—the concentration of each of the phases variescontinuously from one face of the article to the other along acontinuous controlled gradient.

As “dense” ceramic membrane material (A) and “porous support” material Bthat are used in these applications, there are, for example, in the caseof material (B) either carbides or nitrides such as silicon carbide SiCor silicon nitride Si₃N₄, alumina Al₂O₃, aluminum silicates or theirderivatives such as mullite (2SiO₂.3Al₂O₃), SiAlON or cordierite(Mg₂Al₄Si₅O₁₈), magnesia (MgO), or calcium phosphates and itsderivatives such as hydroxyapatite [Ca₄(CaF)(PO₄)₃], tricalciumphosphate [Ca₃(PO₄)₂] or undoped ceramic oxides such as zirconia (ZrO₂)or ceria (CeO₂) or a mixture of one or more of these compounds. The“dense” ceramic membrane material A, in the applications describedabove, is either a purely ionic conductor or a mixed ionic/electronicconductor of cubic phase, fluorite phase, perovskite phase, ofbrown-millerite phase, of the Aurivillius-type family or of pyroclorephase. The figures appended to this description illustrate the inventionwithout however limiting it.

FIG. 1 is a collection of the various steps of the method for producinga ceramic membrane formed mainly from a thin material (A) having asurface concentration gradient of a material (B).

FIG. 2 illustrates the method of preparing a ceramic membrane mainlyformed from a thin material (A) having a surface concentration gradientof a material (B). The steps are the following:

-   -   1) Production of a porous pore-forming substrate by tape        casting, on a flexible plastic film (Mylar™ for example), of a        suspension of pore-forming particles (solvent+pore        formers+organics);    -   2) Evaporation of the solvent;    -   3) Infiltration of the porous pore-forming substrate by a        ceramic suspension of controlled viscosity and controlled        Theological behavior. The viscosity and the Theological behavior        determine the infiltration of the suspension into the porous        pore-forming substrate and therefore the porosity gradient;    -   4) Evaporation of the solvent;    -   5) Cutting of the tape;    -   6) Debinding-sintering or debinding-presintering;    -   7) Total or partial filling of the pores created on the surface        of material (A) with a material (B) or a precursor of material        (B); and    -   8) Binding and sintering or debinding and cosintering of the A+B        combination.

FIG. 3 is a photograph obtained by scanning electron microscopy of thesurface of a porous pore-forming substrate consisting of a stack ofmicronized polypropylene wax particles 25 μm in size, manufactured byMicroPowders, Inc.)

FIG. 4 is a collection of various photographs obtained by scanningelectron microscopy of polished sections of sintered material (A)obtained by infiltration of a porous pore-forming substrate by a BICOVOX10 suspension (material (A)). The BICOVOX 10 suspension is formed fromabout 30 to 50 g of BICOVOX 10 powder (particle size<1 μm), 0.2 g to 2 gof BEYCOSTAT™ A259 dispersant sold in France by CECA—Atochem, 0.5 g to 5g of DEGALAN™ LP 51/07 binder sold in France by Degussa—Hüls and 0.5 gto 5 g of dibutyl phthalate in a methyl ethyl ketone/ethanol mixture sothat the volume ratio of dry matter to the volume of solvent is between25% and 35%. The substrate consists of a stack of 25 μm micronizedpolypropylene wax particles (MicroPowders Inc.) with a variableproportion of organic materials ensuring cohesion of the particles. Thisexample illustrates the effect of the composition of the porouspore-forming substrate on the infiltration of a ceramic tape-castingsuspension. The total porous zone was estimated to be approximately 60%by image analysis.

FIG. 5 is a photograph obtained by scanning electron microscopy of apolished section of the interface between two ceramic materials A and B,BICOVOX. 10 (A) and a material (B) of perovskite structure,respectively. This interface has a structure of the A/A+B/B typeobtained by infiltration of the pores of a ceramic membrane of material(A) by a suspension of material (B); the whole assembly is thencosintered. The ceramic membrane of material (A) was produced beforehandby infiltration of a porous pore-forming substrate consisting ofpore-forming particles having a diameter from 10 to 15 μm, then bindingand sintering. Material (A) is dense. Material (B) has a final porosity,said material being sintered at the sintering temperature (700 to 800°C.) of material (A), a temperature below the sintering temperature ofmaterial (B). It may be considered that a porous electrode layer B hasbeen deposited on a dense support A.

FIG. 6 illustrates the manufacture of porous/dense/porous multilayerelements by thermocompression, in the green state, of a stack of twoback-to-back tapes of a material (A), which tapes are produced by themethod of infiltrating a porous pore-forming substrate with a suspensionof ceramic material A. A material (B) is then deposited in the pores ofthe ceramic article.

It will be understood that many additional changes in the details,materials, steps and arrangement of parts, which have been hereindescribed in order to explain the nature of the invention, may be madeby those skilled in the art within the principle and scope of theinvention as expressed in the appended claims. Thus, the presentinvention is not intended to be limited to the specific embodiments inthe examples given above.

1. A solid-state electrolyte or mixed ionic/electronic conductorapparatus that comprises: a) a thin solid composition consisting of atleast one component selected from the group consisting of ceramic andmetallic material; and b) a surface concentration consisting of at leastone component selected from the group consisting of ceramic and metallicmaterial; wherein the metallic material in part a) is different from themetallic material in part b); wherein said mixed ionic/electronicconductor forms a mixed ionic/electronic conducting ceramic membrane;wherein said membrane comprises material (A) selected from the materialsof the brown-millerite family of formula (III):[Mc_(2-x)Mc′_(x)][Md_(2-y)Md′_(y)]O_(6-w)  (III) wherein Mc is at leastone metal selected from the group consisting of alkaline-earth metals;wherein Mc′ is at least one metal selected from the group consisting oflanthanides and actinides; wherein Md is selected from the groupconsisting of 3d transition metals, and group 13 metals; wherein Md′ isselected from the group consisting of 3d transition metals, group 13metals, lanthanides, and actinides; wherein x and y are identical ordifferent, and are in the range of about 0 about 2; wherein w is suchthat the structure is electrically neutral; wherein a dense phase with acontrolled surface porosity gradient is supported by a material (B);wherein said material (B) is at least one component selected from thegroup consisting of carbides, nitrides, aluminum silicates and theirderivatives, calcium phosphates and their derivatives; and whereinundoped ceramic oxides provide a porous support.
 2. The apparatusaccording to claim 1, wherein said solid-state electrolyte forms anelectrochemical cell.
 3. The apparatus according to claim 1, whereinsaid Mc is selected from the group consisting of Mg, Ca, Sr and Ba. 4.The apparatus according to claim 1, wherein Mc′ is selected from thegroup consisting of La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm,Yb, Lu, and Y.
 5. The apparatus according to claim 1, wherein saidundoped ceramic oxides are selected from the group consisting of ZrO₂and CeO₂.
 6. The apparatus according to claim 1, wherein said material Ais selected from at least one of the formulas in the group consistingof:a) [Mc_(2-x)La_(x)][Md_(2-y)Fe_(y)]O_(6-w)  (IIIa);b) [Sr_(2-x)La_(x)][Ga_(2-y)Md′_(y)]O_(6-w)  (IIIb); andc) [Sr_(2-x)La_(x)][Ga_(2-y)Fe_(y)]O_(6-w)  (IIIc).
 7. The apparatusaccording to claim 2, wherein said apparatus further comprises applyinga reforming catalyst to the external face of the dense phase of material(A).
 8. The apparatus according to claim 2, wherein said solid-stateelectrolyte is utilized for at least one function selected from thegroup consisting of extracting oxygen from a gas mixture containingoxygen and analyzing the presence of oxygen in a gaseous atmosphere. 9.The apparatus according to claim 2, wherein said apparatus producesultrapure oxygen by separating oxygen from air by ionic conductionthrough an electrochemical cell.
 10. The apparatus according to claim 1,wherein said apparatus is utilized for producing thermal and electricalenergy within a solid-state fuel cell, by the reaction of oxygen withhydrogen, and wherein said oxygen is obtained by separating it from air,and by ionic conduction through a ceramic membrane.
 11. The apparatusaccording to claim 1, wherein said membrane is a catalytic membranereactor that produces syngas by the catalytic reaction of natural gas.12. The apparatus according to claim 11, wherein said reaction furthercomprises steam and oxygen, and wherein said oxygen is obtained byseparating it from air, and by mixing ionic/electronic conductionthrough said membrane.
 13. The apparatus according to claim 1, whereinsaid membrane synthesizes an organic compound from hydrocarbon-basedmolecules, comprising at least one oxidation step, catalytic,non-catalytic, using gaseous oxygen, and wherein said oxygen is obtainedby separating it from air, by mixed ionic/electronic conduction throughsaid membrane.
 14. The apparatus according to claim 1, wherein saidmembrane is utilized for gases, liquids, ceramic-to-metal seals,biomaterials and sensors.